KR20150095714A - Rare-earth permanent magnetic powders, bonded magnet comprising same, and device using bonded magnet - Google Patents

Abstract

The present invention provides a device using a rare earth permanent magnet powder, an adhesive magnetic body including the same, and an adhesive magnetic body. The rare earth permanent magnet powder has a 70 to 99 vol% hard magnetic phase having a TbCu ₇ structure and a crystal grain size of 5 to 100 nm, a Fe phase having a bcc structure, an average grain size of 1 to 30 nm and a standard deviation of size of 0.5 And 1 to 30 vol% of soft magnetic phase. The rare-earth permanent magnet powder is a two-phase magnet powder formed by combining a hard magnetic phase having a TbCu ₇ structure and a soft magnetic phase having an α-Fe structure, and the two-phase magnet powder has a uniform microstructure, Thereby ensuring uniform coupling with the phase and improving the magnetic performance.

Description

BACKGROUND OF THE INVENTION 1. Field of the Invention [0001] The present invention relates to a permanent magnet powder, a rare earth permanent magnet powder, an adhesive magnetic substance containing the rare earth permanent magnet powder,

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a rare earth magnetic material, and more particularly to a rare earth permanent magnet powder, an adhesive magnetic material containing the same, and an adhesive magnetic material.

The adhesive rare earth permanent magnet body is a combination of the rare earth permanent magnet powder and the adhesive material and forms various permanent magnet elements by direct injection or compression molding according to the demand of the user. This type of magnetic material has advantages of high size accuracy, excellent magnetic uniformity, good corrosion resistance, high yield, easy processing of a complicated shape device, and the like, , Automobiles, magnetic machines and other devices and devices.

At present, the adhesive rare earth permanent magnet powder mainly includes neodymium magnetite (NdFeB) powder and nitride rare earth magnet powder and the like. Recently, electric vehicles, wind power generators and magnetic levitation trains have been developed to provide higher performance and higher safety for rare earth permanent magnets. Since the nitride rare earth magnet powder has advantages such as high magnetic performance and good corrosion resistance, it has been gradually used widely, and at the same time, research on how to improve the performance of the nitride rare earth magnet powder to meet the application needs is being carried out. Respectively.

The rare earth magnet powder is obtained by nitriding the rare earth alloy powder at a predetermined temperature and for a given time. There are various methods for producing the rare earth alloy powder. The mechanical alloying method can be used and the rapid cooling method can be used. For example, CN1196144C and JP2002057017 disclose an isotropic SmFeN powder magnetic material for producing a resin-adherent magnetic material. Its crystalline structure is TbCu ₇ type. Powder is prepared by dissolving an alloy and rapidly cooling the obtained alloy powder and directly nitriding the obtained alloy powder in a nitrogen- .

US5750044 discloses a nitride rare earth powder which is rapidly cooled and then nitrided. The magnet powder has soft magnetic phase structure with TbCu _7, Th ₂ Zn ₁₇ or Th ₂ Ni _17, and soft magnetic phase proportions 10 to 60%. Although such a nitride rare earth powder can improve the magnetic performance of the nitride rare earth magnet powder to a certain extent, a study should be conducted to further improve the magnetic performance of the rare earth permanent magnet powder in order to meet the demand for high quality products of users.

An object of the present invention is to provide a rare earth permanent magnet powder, an adhesive magnetic body and a device using the adhesive magnetic body, which can improve the magnetic performance of the rare earth permanent magnet powder.

In order to achieve the above object, according to one aspect of the present invention, there is provided a magnetic recording medium comprising a hard magnetic phase (70 to 99 vol%) having a crystal grain size of 5 to 100 nm having a TbCu ₇ structure, a Fe phase having a bcc structure, A rare earth permanent magnet powder comprising 1 to 30 vol% of soft magnetic phase (soft magnetic phase) having a size of 1 to 30 nm and a standard deviation of size of less than 0.5σ.

In the rare earth permanent magnet powder, the hard magnetic phase crystal grain size is distributed in the range of 5 to 80 nm, and preferably the hard magnetic phase crystal grain size is distributed in the range of 5 to 50 nm.

In the rare earth permanent magnet powder, the soft magnetic phase accounts for 3 to 30 vol% of the total volume of the rare earth permanent magnet powder, and preferably the soft magnetic phase accounts for 5 to 15 vol% of the total volume of the rare earth permanent magnet powder.

In the rare-earth permanent magnet powder, the soft magnetic phase has an average crystal grain size of 1 to 20 nm.

In the rare earth permanent magnet powder, the standard deviation of the soft magnetic phase crystal grain size is 0.3 이하 or less.

The rare-earth permanent magnet powder is composed of RTMA, R is a combination of Sm or Sm and other rare earth elements, T is Fe or a combination of Fe and Co, M is Ti, V, Cr, Zr, Nb, Mo, Ta, W, Si or Hf, A is N and / or C, and preferably, the content of R is 5 to 12 at.%, The content of A is 10 to 20 at.%, To 10 at.%, And the remainder is T.

In the rare earth permanent magnet powder, the content of R is 5 to 10 atomic%.

Further, in the rare-earth permanent magnet powder, the content of atomic number of Sm in R is 80 to 100 atomic%.

Further, in the above rare earth permanent magnet powder, T is a combination of Fe and Co, and the content of Co atomic number in T is 0 to 30 at.%.

The rare earth permanent magnet powder has a thickness of 5 to 50 탆.

According to a second aspect of the present invention, there is provided an adhesive magnetic body formed by bonding an adhesive to the rare earth permanent magnet powder.

According to a third aspect of the present invention, there is provided a device using the adhesive magnetic body.

According to a fourth aspect of the present invention, there is provided a method of manufacturing a honeycomb structured body, comprising the steps of: injecting a molten raw material into a rotating roller and subjecting the honeycomb structure to rapid cooling treatment to produce a flaky alloy powder; in the production process comprising the step of obtaining a rare earth permanent magnet powder, rapidly the step of generating via the cooling processing piece-type alloy powder, sprayed onto the rotating dissolved raw material roller and ^{1 × 10 5 ℃ / s ~} 80 × A first cooling is performed at a cooling rate of 10 ⁵ ° C / s to 850 ° C to 950 ° C, and a second cooling is performed at a cooling rate of 0.5 ° C / s to 5 ° C / s to 250 ° C to 350 ° C To obtain a rare earth permanent magnet powder, which comprises obtaining a piece-shaped alloy powder.

Also, in the above-mentioned method, the temperature of the flake alloy powder is raised at a rate of 10 ° C / s to 30 ° C / s, and the temperature is raised to 600 to 900 ° C, followed by heat treatment for 10 to 150min , And it is preferable to raise the temperature of the flake alloy powder at a rate of 10 ° C / s to 20 ° C / s.

The rare-earth permanent magnet powder of the present invention is a two-phase magnet powder formed by combining a hard magnetic phase having a TbCu ₇ structure and a soft magnetic phase having an? -Fe structure, and the two-phase magnet powder has a uniform microstructure, Uniform coupling between the magnetic phase and the hard magnetic phase can be ensured and the magnetic performance of the rare earth permanent magnet powder can be improved.

Here, the features described in the embodiments and the embodiments of the present application can be combined with each other under a situation where they do not collide with each other. The present invention is explained in detail by combining the following examples.

The microstructure of the rare earth permanent magnet powder plays a very important role in the performance of the material, and due to a certain microstructure, various factors such as the bonding action between the crystal grains of the magnetic material, the formation of the magnetic region and the stability of the structure are determined. This will affect performance. The inventors of the present invention have studied the microstructure of the rare earth permanent magnet powder in order to improve the magnetic performance of the rare earth permanent magnet powder,

The rare earth permanent magnet powder of the present invention is composed of 70 to 99 vol% of a hard magnetic phase and 1 to 30 vol% of a soft magnetic phase, the hard magnetic phase has a TbCu ₇ structure, the crystal grain size is 5 to 100 nm, the average size of the soft magnetic phase crystal grains is 1 to 30 nm and the standard deviation of the size is 0.5 or less.

The rare-earth permanent magnet powder provided in the present invention is a two-phase magnet powder formed by combining a hard magnetic phase having a TbCu ₇ structure and a soft magnetic phase having an? -Fe structure. In such a rare earth permanent magnet powder, the hard magnetic phase having a TbCu ₇ structure has a magnetic property superior to that of the widely used nitride magnet powder of Th ₂ Zn ₁₇ structure and ThMn ₁₂ structure, Is more advantageous for the improvement of. At the same time, the coupling action between the hard magnetic phase having a soft magnetic phase and a TbCu ₇ structure on Fe having a bcc structure is generated to suppress the performance is TbCu ₇ structure, call structures, Th ₂ Zn _17, and a rare earth permanent magnet powder Crystallization and nitrification steps to prevent Th ₂ Zn ₁₇ and ThMn ₁₂ phases from forming and deteriorating magnetic performance. And the Fe phase with the bcc structure is soft magnetic phase, which has a certain residual magnetic strengthening effect and slows the sensitivity of the magnet powder to temperature and extends the range of manufacturing steps.

In order to realize the above-described coupling effect between the soft magnetic phase and the hard magnetic phase, it is preferable that the size of hard magnetic phase crystal grains in the rare earth permanent magnet powder of the present invention is 5 to 100 nm. This is because in the rare earth permanent magnet powder, when the average crystal grain size of the hard magnetic phase is less than 5 nm, it is disadvantageous in obtaining a coercive force of 5 kOe or more, and the manufacturing difficulty is greatly increased and the yield is lowered. And if the average crystal grain size on the hard magnetic exceed 100nm can not result in the hard magnetic phase α-Fe phase and the combined action with the TbCu ₇ structure at the same time to lower the residual magnetism on the hard-magnetic α-Fe is TbCu ₇ structure is Th _{2 < RTI ID = 0.0 >} Zn ₁₇ < / RTI > structure, as well as deteriorating performance. In order to improve the magnetic performance of the rare earth permanent magnet powder of the present invention, the hard magnetic phase crystal grain size is more preferably distributed in the range of 5 to 80 nm and in the range of 5 to 50 nm.

In the rare earth permanent magnet powder of the present invention, it is preferable that the soft magnetic phase content is 1 to 30 vol%. When the soft magnetic phase volume is controlled within this range, the TbCu ₇ structure can be inhibited from being converted to the Th ₂ Zn ₁₇ structure and the magnetic performance of the rare earth permanent magnet powder produced can be improved. If the content of soft magnetic phase is less than 1 vol%, the effect of suppressing the occurrence of other miscellaneous matters deteriorates. If the content of soft magnetic phase exceeds 30 vol%, generation of other miscellaneous phases such as Th ₂ Zn ₁₇ can be suppressed. There is a problem of greatly reducing the coercive force of the material and it is disadvantageous to improve the overall performance. In order to improve the magnetic performance of the rare-earth permanent magnet powder of the present invention, the proportion of the soft magnetic phase is preferably 3 to 30 vol%, more preferably 5 to 15 vol%.

In the rare earth permanent magnet powder of the present invention, it is preferable that the average crystal grain size? Of the soft magnetic phase is 1 to 30 nm and the effect of reinforcing the residual magnet is controlled by controlling the average crystal grain size? It is possible to improve the magnetic performance of the rare earth permanent magnet powder. If the mean crystal grain size? Of the soft magnetic phase is too large, it is not possible to realize the reinforcing action of the residual magnetism, and there is a possibility of reducing the coercive force of the magnet powder. If the soft magnetic phase average crystal grain size? Is too small, the manufacturing difficulty becomes high. It is more preferable that the soft magnetic phase has an average crystal grain size of 1 to 20 nm in the rare-earth permanent magnet powder.

In the rare earth permanent magnet powder of the present invention, the standard deviation of the soft magnetic phase crystal grain size is less than 0.5σ. In the magnet powder, the distribution of the soft magnetic phase is also a key factor affecting the magnetism of the magnet powder. In the uniform structure, the soft magnetic phase and the hard magnetic phase are uniformly mixed and the bonding condition is good and the magnetic performance is improved Do. When the standard deviation of the average crystal grain size of the soft magnetic phase in the rare-earth permanent magnet powder of the present invention is controlled to 0.5 이하 or less, it is possible to uniformly combine the soft magnetic phase and the hard magnetic phase, . If the standard deviation of the soft magnetic phase crystal grain size exceeds 0.5σ, the distribution of the crystal grains is so wide that a uniform and precise structure can not be obtained, the exchange function between each particle in the magnet powder is lowered and the residual magnetism (Br) The coupling with the hard magnetic phase and the reinforcement effect of the residual magnetic force can not be realized, and finally good magnetic performance can not be obtained. In the rare-earth permanent magnet powder of the present invention, it is preferable that the standard deviation of the soft magnetic phase crystal grain size is 0.3 σ.

In a preferred embodiment of the present invention, the rare earth permanent magnet powder is composed of RTMA, where R is a combination of Y or Y and other rare earth elements, T is Fe or a combination of Fe and Co, M is Ti, V, At least one of Cr, Mn, Ni, Cu, Zr, Nb, Mo, Ta, W, Al, Ga, Si or Hf. In the rare earth permanent magnet powder, it is preferable that the content of R is 5 to 12 at.%, The content of A is 10 to 20 at.%, The content of M is 0 to 10 at.%, And the remainder is T.

In the rare earth permanent magnet powder composed of the RTMA of the present invention, the R element is a combination of Sm or Sm and other rare earth elements, R is a combination of Sm or Sm and other rare earth elements, where R must include Sm, which is TbCu ₇ structure and to ensure magnetic performance.

The content of the R element is preferably in the range of 5 to 12 at.%, More preferably in the range of 5 to 10 at.%. If the atomic content of R in the rare-earth permanent magnet powder is less than 5 at.%, The formation of the? -Fe soft magnetic phase is relatively large and the coercive force of the produced magnet powder is lowered. When the content of R exceeds 12 at.%, Many similar structures are formed on the samarium, and these two situations are all disadvantageous for the improvement of the magnetic performance. In the rare earth permanent magnet powder of the present invention, the content of atomic number of Sm is preferably 80 to 100 at.%, The partial Sm may be substituted with rare earth elements such as Ce and Y, the proportion of substitution is 20% When the rare earth element is added, the forming ability of the material can be opened. For example, when Ce and La are added, the content of Ce and La should be less than 5 at.%. When Nd and Y are added, coercive force Can be improved.

In the rare earth permanent magnet powder constituted by the RTMA of the present invention, the T element is preferably Fe or a combination of Fe and Co, and T is a combination of Fe and Co. Addition of a certain amount of Co is advantageous for improving the residual magnetism and temperature stability of the nitrogen-containing magnet powder, and is advantageous for stabilizing the structure of the TbCu ₇ phase and improving the water absorbability and the like during production. Considering the causes such as cost, the content of Co in T is 0 to 30 at.% And the content of Co is 0 at.%, It means that Co is not contained.

In the rare earth permanent magnet powder constituted by the RTMA of the present invention, element M may be added. In the present invention, all of the elements M are higher than rare earth Sm, and when such element having a high melting point is added, An advantageous and particularly uniform rare earth permanent magnet powder is formed and the non-uniform growth of the crystal grains during crystallization or nitriding is suppressed, and the standard deviation of the size of the magnet powder crystal grains of the present invention is within a certain range. M includes one or more of Ti, V, Cr, Mn, Zr, Nb, Mo, Ta, W, Si, and Hf, but is not limited thereto. When M is added, the crystal grains are subdivided and coercive force Thereby improving magnetic performance such as magnetism. At the same time, in the rare earth permanent magnet powder, the atomic content of the M element is preferably 0 to 10 at.%, And if the atomic content of the M element exceeds 10 atomic%, the magnetic properties such as residual magnetism may be deteriorated.

In the rare earth permanent magnet powder composed of the RTMA of the present invention, when element A is added and A is N and / or C and the element A is added to the rare earth iron compound, the performance is greatly affected. It is called. According to the interstitial atom effect, the rare earth permanent magnet powder which can improve the Curie temperature, the saturation magnetization intensity and the anisotropic magnetic field of the compound and is composed of the RTMA of the present invention preferably contains 10 to 20 atomic% of A atoms If the content is less than 10 at.%, It is indicated that the component is not uniform and the magnetic property is deteriorated because the nitriding / carbonation is insufficient, and if it is too high, the hard magnetic phase decomposes Which is disadvantageous for improvement of magnetic performance.

In a preferred embodiment of the present invention, the rare-earth permanent magnet powder is composed of a hard magnetic phase having a TbCu ₇ structure and an Fe phase having a bcc structure, wherein the soft magnetic phase of the bcc structure is mainly an? -Fe phase and the Cu target The number of diffraction peaks in which the ratio of the peak intensity with the 2? Angle of 65 to 75 and the highest peak intensity in the X-ray diffraction diagram using 10% or more is less than 1. When the number of diffraction peaks satisfying this condition is one or zero, the size and distribution of the crystal grains in the produced adhesive magnetic powder are within the limits defined by the present invention and have optimum blending performance.

In a preferred embodiment of the present invention, the thickness of the rare-earth permanent magnet powder is less than 50 mu m. By controlling the thickness of the magnet powder, it is advantageous to uniform distribution of each phase in the magnet powder, and optimization of performance such as magnet powder square ratio of the magnet powder can be realized. When the thickness exceeds 50 탆, it is indicated that the crystal of each phase in the material is not uniformly distributed, and the performance of squareness ratio of the magnetic powder is finally deteriorated, and nitrogen or carbon penetrates into the material crystal during nitriding. It is preferable that the thickness of the rare earth permanent magnet powder is 5 to 50 mu m, and if the thickness is too small, the manufacturing difficulty is high, the amorphous body becomes large, and it is disadvantageous to maintain the consistency of the subsequent crystallization or nitriding step.

In the present invention, the rare earth permanent magnet powder can be manufactured by a rapid cooling method and a person skilled in the art can produce a rare earth permanent magnet powder satisfying the above requirements under the guidance of the present application. Currently widely used manufacturing methods include the following steps: (1) For example, each raw material component such as R, T, M, and A is melted and sprayed onto a rotating roller through a nozzle to obtain a flaky alloy powder, 2) performing a heat treatment at 600 to 900 ° C. for 10 to 150 minutes on the powdered alloy powder; and (3) nitriding or carbonizing the alloy powder after the heat treatment at a temperature of about 350 to 550 ° C. to obtain a rare earth permanent magnet powder.

Those skilled in the art will appreciate that, in the preferred embodiment of the present application, in order to manufacture the rare earth permanent magnet powder to be protected by the present invention and to improve the performance of the rare earth permanent magnet powder produced by lowering the work difficulty level, To obtain a rare earth permanent magnet powder by performing a rapid cooling treatment on the rare earth magnet powder to produce a flaky alloy powder, subjecting the flaky alloy powder to a heat treatment, and then performing a nitriding or carbonization treatment to obtain a rare earth permanent magnet powder . Here, in the step of performing the rapid cooling treatment to produce the flake alloy powder, the melted raw material is sprayed onto a rotating roller and heated at a cooling rate of 1 × 10 ⁵ ° C./s to 80 × 10 ⁵ ° C./s from 850 ° C. to 950 And then performing a second cooling in which the first cooling is performed at a cooling rate of 0.5 占 폚 / s to 5 占 폚 / s to 250 占 폚 to 350 占 폚 to obtain the piece-shaped alloy powder .

In a preferred embodiment of the present invention, the step of performing the rapid cooling treatment to produce the flaky alloy powder is performed by spraying the melted raw material onto the roller and heating the melted raw material to a temperature of 5 x 10 < ⁵ > A first cooling step of cooling the substrate to a temperature of 880 ° C to 920 ° C at a cooling rate of 10 ⁵ ° C / s and a second cooling step of cooling the substrate to 280 ° C to 320 ° C at a cooling rate of 0.5 ° C / Followed by cooling twice to obtain the engraved alloy powder.

In the present invention, the molten steel liquid is injected through a rotating roller and rapidly cooled to 850 캜 to 950 캜. In this step, the rapid cooling rate is 1 x 10 ⁵ 캜 / s to 80 x 10 ⁵ 캜 / s, and the equilibrium phase is not formed due to the cooling rate, and the size of the crystal grains is not yet grown. In a preferred embodiment of the present invention, a guide plate is added in the direction in which the flaky powder is injected so that the steel liquid is injected after the treatment and reaches a cooling rate of 0.5 ° C / s to 5 ° C / s for cooling twice The cooling rate of the flaky powder is controlled by controlling the distance between the guide plate and the starting point of injection of the flaky powder and the temperature of the guide plate.

According to the method for producing a rare earth permanent magnet powder provided in the present invention, it is possible to obtain a precise structure through a rapid cooling step of cooling twice, and at the same time, the material is cooled at a low cooling rate during twice cooling, And the crystal grain size of the rare earth alloy powder does not grow too unevenly during the heat treatment and the magnetic performance of the final rare earth permanent magnet powder can be ensured.

In the preferred embodiment of the present invention, in the method of manufacturing the rare earth permanent magnet powder, the temperature of the flake alloy powder during the heat treatment is raised to 600 to 900 ° C at a rate of 10 ° C / s to 30 ° C / To 850 DEG C, and then a heat treatment is performed for 10 to 150 minutes, wherein it is preferable to raise the temperature of the flake alloy powder at a rate of 10 DEG C / s to 20 DEG C / s. If it is raised at a constant speed, it is advantageous to maintain the stability in the entire heating section and the powder grows uniformly. If the speed is too slow, the heating time of the powder is long and it is disadvantageous to control the heat treatment process. If the speed is too high, the heating of the powder is uneven. The preferred heat treatment temperature of the present invention is 600 to 900 DEG C, and if it is too high, the crystal grains grow too much and if too late, the heat treatment effect can not be realized.

In the material of the rare-earth permanent magnet powder of the present invention, the material of the roller preferably includes Cu, Mo, and Cu alloys, but is not limited thereto. It is also preferable that the nitridation or carbonization step has a nitridation or carbonization time of 3 to 30 hours, and that the nitrogen source is a pure nitrogen gas, a mixed gas of hydrogen and ammonia gas, or the like.

In a preferred embodiment of the present invention, the rare earth permanent magnet powder may be bonded to an adhesive to form an adhesive magnetic body. Such an adhesive magnetic body is prepared by mixing, compressing, injecting, rolling or extruding the rare earth permanent magnet powder of the present invention (the main phase is a SmFeN powder having a TbCu ₇ structure) and a resin. The adhesive magnetic body to be produced may be formed into other shapes such as massive, annular, and the like.

In the preferred embodiment of the present invention, the adhesive magnetic body can be applied to the manufacture of a corresponding device. According to this method, a high-performance SmFeN magnet powder and a magnetic substance can be manufactured, the device can be further downsized, Since the magnet powder has high heat resistance and corrosion resistance, it is advantageous to use the device in special environment, and it is advantageous for equilibrium application of rare earth resources by applying rare earth samarium.

Hereinafter, the rare earth permanent magnet powder component, the crystal grain size, the crystal grain distribution, the performance of the magnetic powder, the performance of the magnetic body, etc. of the present invention will be described in the manner of a concrete example to illustrate the beneficial effects of the present invention.

(1) Rare earth permanent magnet powder component

The components of the rare earth alloy magnet powder are formed by nitriding the alloy powder of the samarium iron series, and the component is a component of the magnetized powder after nitriding and the component is expressed in atomic%.

(2) Crystal grain size?

Representation of average crystal grain size: A microstructure photograph of the material was taken with an electron microscope, and the crystal grains of the TbCu ₇ structure and the soft magnetic α-Fe crystal grains were observed from the photographs. The total cross-sectional area S of the crystal grains of the crystal grains is calculated, and if a circle having the same area as the cross-sectional area S is obtained, the diameter of the circle is the average crystal grain size?

이다.

to be.

(3) Distribution of crystal grains

The distribution of the crystal grains is represented by the standard deviation, and the corresponding equation

이다.

to be.

는 제i번째 결정입자의 사이즈이다. Where T is the standard deviation

Is the size of the i-th crystal grain.

In the present invention, n takes a value of 50 or more in consideration of the statistical accuracy and the test situation.

(4) Performance of magnet powder

The performance of the magnet powder is detected by a sample vibration magnetic flux meter (VSM detection).

Here, Br is the residual magnet and the unit is kGs.

Hcj is the inherent coercivity and the unit is kOe.

(BH) m is the magnetic energy product and the unit is MGOe.

(5) Phase proportional P%

The phase ratio is obtained by analyzing the area of the gold image of the magnetic material. The volume ratio can be obtained by measuring the cross-sectional area ratio.

(6) XRD peak

The obtained alloy powder was measured by XRD and the target of the Cu target was observed, and the phase structure of the obtained magnet powder was observed.

As a result of performing XRD peak detection on the rare earth permanent magnet powder prepared in the following Examples 1 to 38, it was found that the diffraction peaks in which the ratio of the peak intensity with the 2 &thetas; angle of 65 DEG to 75 DEG to the strongest peak intensity exceeded 10% Of the total number is one or zero.

(7) Thickness?

The thickness is measured with a micrometer caliper and the unit of thickness is μm.

Examples 1 to 8 (M is one or two elements)

Manufacturing method:

(1) The metals described in the examples of Table 1 are mixed according to proportions and introduced into an induction furnace and dissolved under the protection of an Ar gas to obtain an alloy ingot.

(2) The alloy ingot was roughly pulverized and put into a rapid cooling furnace to be rapidly cooled. The protective gas was Ar gas, the injection pressure was 80 kPa, the diameter of the nozzle was 0.8 mm, the linear velocity of the water-cooling roller was 55 m / s, Thereafter, a piece-shaped alloy powder is obtained.

(3) The alloy powder is subjected to a nitriding treatment under N ₂ gas at atmospheric pressure at 750 ° C for 55 minutes under the protection of an Ar gas (treatment conditions are 460 ° C for 7 hours) to obtain a nitride magnet powder.

Detection: The magnetic performance, crystal grain size, crystal grain distribution, and phase proportions of the rare earth permanent magnet powder (the ingredients of which are shown in Table 1) were detected. The results of the detection are shown in Table 2 (material structure and performance), S indicates an example, and D indicates a comparative example.

It can be seen from the above examples that a high magnetic performance can be obtained when the crystal grain size and distribution of the magnet powder are within the protection range of the present invention, and they are mainly embodied by the coercive force and the magnetic energy product. When D1 and D2 are compared, when the crystal grain size and distribution are deviated from the protective range, even when the? -Fe soft magnetic phase exists in the magnet powder, the crystal grains are large and the distribution is uneven, Coercivity also drops significantly. Here, the soft magnetic phase crystal grains of D1 exceeded 30 nm and t > 0.5 sigma of D2, and all of the magnetic properties were greatly deteriorated. At the same time, when the standard deviation of the soft magnetic phase crystal grain is distributed to t? 0.5? S, the performance is high and the performance is the highest when t? At the same time, when comparing the embodiment of the present application with D3, the magnetic properties are drastically lowered when the hard magnetic phase grains are too large. In this embodiment, the hard magnetic phase grains are all in the range of 5 to 50 nm, . Here, when the hard magnetic phase crystal grain size is in the range of 5 to 80 nm, particularly when the hard magnetic phase crystal grain size is distributed in the range of 5 to 50 nm, the magnetic performance is better.

Examples 9 to 13 (M is a mixture of many elements)

Manufacturing method:

(1) The metals described in each of Examples in Table 3 are mixed according to proportions and introduced into an induction melting furnace and dissolved under the protection of Ar gas to obtain an alloy ingot.

(2) The alloy ingot was roughly pulverized and put into a rapid cooling furnace to be rapidly cooled. The protective gas was Ar gas, the injection pressure was 80 kPa, the diameter of the nozzle was 0.8, the linear velocity of the water-cooling roller was 55 m / s, To obtain a piece-like alloy powder.

(3) The alloy is treated at 750 ° C for 55 minutes under the protection of Ar gas, and nitrided in N ₂ gas at atmospheric pressure (treatment conditions are 460 ° C for 7 hours) to obtain a nitride magnet powder.

Detection: The magnetic performance, crystal grain size, crystal grain distribution, and phase proportions of the rare earth permanent magnet powder (the components of the materials are shown in Table 3) were detected. The detection results are shown in Table 4 (material structure and performance), S indicates the example, and D indicates the comparative example.

When a large number of M is added from the above Examples and Comparative Examples, the intrinsic magnetic properties are lowered compared with the case where one or two M elements are added. This is because the saturation magnetic moments of the bivalent elements are lower than those of Fe and Co It can be seen that the addition of more elements results in a loss of saturation magnetic moment and a decrease in the magnetic performance of the part.

Similarly, when the crystal grain size and distribution are deviated from the protective range, the coercive force is largely lowered, and even when the? -Fe soft magnetic phase is present in the magnetic powder, the crystal grains are large and the distribution is uneven. From the data in Table 4, it can be seen that the performance is highest when the distribution of the standard deviation of the soft magnetic phase crystal grains is t≤0.5σ, and the performance is the highest when t≤0.3σ.

Examples 14 to 16 (SmFeN type permanent magnet powder)

Manufacturing method:

(1) The SmFe alloys of the respective examples shown in Table 5 are mixed according to a predetermined proportion and introduced into an induction furnace and dissolved under the protection of an Ar gas to obtain an alloy ingot.

(2) The alloy ingot is roughly pulverized and put into a rapid cooling furnace to be rapidly cooled. The protective gas is Ar gas, the injection pressure is 100 kPa, the diameter of the nozzle is 0.8 mm, the linear velocity of the water-cooling roller is 55 m / s, Thereafter, a piece-shaped alloy powder is obtained.

(3) The alloy powder is nitrided under N ₂ gas at atmospheric pressure at a temperature of 730 캜 for 60 minutes under the protection of an Ar gas (treatment conditions are 440 캜 for 8 hours) to obtain a nitride magnet powder.

Detection: The magnetic performance, crystal grain size, crystal grain distribution, and phase proportions of the rare earth permanent magnet powder (the ingredients of which are shown in Table 5) were detected. The results of the detection are shown in Table 6 (material structure and performance), S indicates the example, and D indicates the comparative example.

When Co and biboidal metal M are not added to the magnet powder prepared from the data in Table 6, the performance is high when soft magnetic phase crystal grains are high and magnetic performance is low, but the distribution of crystal grains is t? 0.5? 0.3 σ is the highest performance.

Examples 17 to 21 (SmRFeCoMN type magnet powder)

Manufacturing method:

(1) The relevant rare earth and transition metal described in each of Examples in Table 7 are mixed in a proportional proportion and introduced into an induction furnace and dissolved under the protection of Ar gas to obtain an alloy ingot.

(2) The alloy ingot is roughly pulverized and injected into a rapid cooling furnace to rapidly cool. The protective gas is Ar gas, the injection pressure is 80 kPa, the diameter of the nozzle is 0.7 mm, the linear velocity of the water-cooling roller is 55 m / s, ) The diameter of the roller is 300 mm, and after rapid cooling, a piece-like alloy powder is obtained.

(3) The alloy is treated at 700 캜 for 70 minutes under the protection of an Ar gas, and nitriding is performed in an N ₂ gas at atmospheric pressure (treatment condition is 450 ° C for 6 hours) to obtain a nitride magnet powder.

Detection: The magnetic properties, the crystal grain size, the crystal grain distribution, and the phase proportion of the rare earth permanent magnet powder (ingredients of the materials are shown in Table 7) were detected. The results of the detection are shown in Table 8 (material organization and performance), S indicates the example, and D indicates the comparative example.

When the rare earth element R is added to the magnet powder prepared from the data in Table 8, the residual magnetism decreases uniformly, but the performance of each side is still high when the distribution of the crystal grains is t? 0.5 ?, and t? ), The performance is the highest. From S19, if the content of the rare earth element is high, the residual magnetic and magnetic energy products are largely lowered but the coercive force is high.

Examples 22 to 30 (permanent magnet powder containing carbon)

Manufacturing method

(1) A high-purity metal is mixed in accordance with the proportions, and the mixture is introduced into an induction melting furnace and dissolved under the protection of an Ar gas to obtain an alloy ingot.

(2) The alloy ingot was roughly pulverized and put into a rapid cooling furnace to rapidly cool. The protective gas was Ar gas, the injection pressure was 80 kPa, the diameter of the nozzle was 0.8 mm, the linear velocity of the water-cooling roller was 50 m / Is 300 mm in diameter, and after the rapid cooling, a piece-shaped alloy powder is obtained.

(3) The alloy is treated under the protection of Ar gas at 710 占 폚 for 70 minutes, the magnet powder is pulverized into particles of 100 占 퐉 or less, the pulverized powder and the carbon powder are mixed and treated at 480 占 폚 for 7 hours to obtain a magnet powder as a carbide .

Detection: The magnetic performance, crystal grain size, crystal grain distribution, and phase proportions of the produced rare-earth permanent magnet powder (the components of the materials are as shown in Table 9) were detected. The detection results are shown in Table 10 (material structure and performance), S indicates an example, and D indicates a comparative example.

The rare-earth permanent magnet powders prepared from the data in Table 10 exhibit high magnetic performance even when the element C is added and the magnetic energy product reaches 15 MGOe or more. At the same time, when the distribution of the crystal grains is t? 0.5 ?, the performance is high and t? The performance is the highest.

Examples 31 to 38

The process for producing the rare earth permanent magnet powder of the present invention is mainly used for the production of Sm _8.5 Fe _bal Co _10.6 Zr _0.8 N _12.5 adhesive magnet powder and the manufacturing steps are as follows:

(1) High purity metals are mixed according to the proportions of the respective examples in Table 11, and the mixture is introduced into an induction melting furnace and dissolved under the protection of Ar gas to obtain an alloy ingot.

(2) The alloy ingot was roughly pulverized and put into a rapid cooling furnace to rapidly cool it. The protective gas was Ar gas, the injection pressure of the nozzle was controlled to 80 kPa, the diameter of the nozzle was 0.8 mm, (The roller material, the rotating speed, the first cooling temperature, and the second cooling temperature are as shown in Table 11).

(3) The alloy is heated and raised while raising the temperature of the flaky alloy powder under the protection of Ar gas, and then the heat treatment is performed while maintaining the temperature (temperature rise rate, temperature after rise, same). The magnet powder is pulverized into particles having a particle size of 100 탆 or less and the pulverized powder is treated in an N ₂ atmosphere to obtain a magnetic powder (the nitriding temperature and the nitriding time are as shown in Table 11).

Detection: The magnetic properties, the crystal grain size, the crystal grain distribution, and the phase proportion of the rare earth permanent magnet powder (ingredients of the materials are as shown in Table 11) were detected. The detection results are shown in Table 10, where S indicates an example and D indicates a comparative example.

The unit of the detection data in the step is as follows:

The unit of temperature rise rate is ° C / s, the unit of cooling rate is ° C / s, the unit of rate of rapid cooling roller is m / s, the unit of crystallization temperature and nitridation temperature is ° C and the unit of crystallization time is min (minute) And the unit of nitriding time is h (hour). Table 11 shows specific manufacturing of the magnet powder and magnetic performance of the final magnet powder, and Table 12 shows the material structure and performance.

The rare earth permanent magnet powder provided in the present invention can be produced by rapid cooling method and those skilled in the art can obtain the rare earth permanent magnet powder to be protected by the present application by using ordinary rapid cooling method and adjusting the parameters of each step, The method used in Examples S1 to S30 can be used. In the present invention, it is preferable to use the rapid cooling treatment step of cooling twice, and it can be seen that a precise structure can be obtained through the rapid cooling treatment step in which the material is cooled twice from the data in Tables 11 to 12, Is cooled at a low rate in the second cooling process, the stability of the size of the crystal grains can be ensured and the crystal grain size of the rare earth alloy powder does not grow too unevenly during the heat treatment, It is possible to obtain a good magnetic performance with a crystal grain distribution of the material to be produced of t? 0.5?.

As described above, according to the composite material of the main phase TbCu ₇ structure and the bcc soft magnetic phase structure of the present invention, the magnetic performance of the material can be improved by controlling the crystal grain size and distribution. According to the present invention, an adhesive magnetic body can be manufactured by mixing the above-mentioned magnet powder and an adhesive to apply to motors, speakers, measuring instruments, and the like.

The foregoing is a preferred embodiment of the present invention and is not intended to limit the present invention. It will be apparent to those skilled in the art that various modifications and variations can be made in the present invention. And all modifications, equivalents, improvements and the like which are within the spirit and principle of the present invention are within the scope of the present invention.

Claims (14)

70 to 99 vol% of a hard magnetic phase having a TbCu ₇ structure and a crystal grain size of 5 to 100 nm,
a Fe phase having a bcc structure, an average crystal grain size of 1 to 30 nm, and a standard deviation of size of less than 0.5σ.
The method according to claim 1,
Wherein the hard magnetic phase crystal grain size is distributed in the range of 5 to 80 nm, and preferably the hard magnetic phase crystal grain size is distributed in the range of 5 to 50 nm.
3. The method according to claim 1 or 2,
Wherein the soft magnetic phase accounts for 3 to 30 vol% of the total volume of the rare earth permanent magnet powder, and preferably the soft magnetic phase accounts for 5 to 15 vol% of the total volume of the rare earth permanent magnet powder.
4. The method according to any one of claims 1 to 3,
Wherein the soft magnetic phase has an average crystal grain size of 1 to 20 nm.
5. A compound according to any one of claims 1 to 4,
Wherein the soft magnetic phase has a standard deviation of the crystal grain size of not more than 0.3σ.
6. A compound according to any one of claims 1 to 5,
T is a combination of Fe or Fe and Co, and M is a combination of Ti, V, Cr, Zr, Nb, Mo, Ta, W, Si, or a combination of Sm and Sm and other rare earth elements. H, A is N and / or C, and preferably, the content of R is 5 to 12 at.%, The content of A is 10 to 20 at.%, The content of M is 0 to 10 at.% And the remainder is T Features rare earth permanent magnet powder.
The method according to claim 6,
And a content of R is 5 to 10 atomic%.
8. The method of claim 7,
Wherein the content of Sm in the R is 80 to 100 at.%.
The method according to claim 6,
T is a combination of Fe and Co, and the content of Co in the T is 0 to 30 at.%.
10. A compound according to any one of claims 1 to 9,
Wherein the thickness of the rare earth permanent magnet powder is 5 to 50 mu m.
10. An adhesive magnetic body formed by adhering an adhesive to a rare earth permanent magnet powder according to any one of claims 1 to 10.
An element characterized by applying the adhesive magnetic body according to claim 11.
A step of adding the molten raw material to a rotating roller and subjecting the molten raw material to a rapid cooling treatment to produce a piece-shaped alloy powder; a step of obtaining the rare earth permanent magnet powder through heat treatment of the piece-shaped alloy powder and then nitriding or carbonizing A method for producing a rare earth permanent magnet powder,
Wherein the step of producing the engraved alloy powder through the rapid cooling treatment comprises:
The first raw material is sprayed onto a rotating roller and cooled to 850 캜 to 950 캜 at a cooling rate of 1 10 ⁵ 캜 / s to 80 10 ⁵ 캜 /
And a second cooling step of cooling to 250 DEG C to 350 DEG C at a cooling rate of 0.5 DEG C / s to 5 DEG C / s to obtain the flaky alloy powder. A method for producing a rare-earth permanent magnet powder as set forth in any one of the preceding claims.
14. The method of claim 13,
Wherein the heat treatment includes raising the temperature of the flake alloy powder at a rate of 10 ° C / s to 30 ° C / s, raising the temperature to 600 to 900 ° C, and performing a heat treatment for 10 to 150 minutes, Preferably, the temperature of the flake alloy powder is raised at a rate of 10 ° C / s to 20 ° C / s.